CN103045937A - Secondary cold rolled steel and production method thereof - Google Patents
Secondary cold rolled steel and production method thereof Download PDFInfo
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- CN103045937A CN103045937A CN2012105446221A CN201210544622A CN103045937A CN 103045937 A CN103045937 A CN 103045937A CN 2012105446221 A CN2012105446221 A CN 2012105446221A CN 201210544622 A CN201210544622 A CN 201210544622A CN 103045937 A CN103045937 A CN 103045937A
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Abstract
The invention discloses a secondary cold rolled steel which comprises the following chemical elements in percentage by mass: 0.005 to 0.015 percent of C, 0.50 to 1.00 percent of Mn, 0.01 to 0.04 percent of Al, 0.004 to 0.0100 percent of N and the balance of Fe and other inevitable impurities. Correspondingly, the invention further discloses a production method for the secondary cold rolled steel. The secondary cold rolled steel, disclosed by the invention, has higher strength, higher hardness and smaller thickness, and also has excellent bake hardening performance and processability.
Description
Technical field
The present invention relates to field of metallurgy, relate in particular to a kind of steel grade and manufacture method thereof.
Background technology
In order to save cost, increasing industry requirement reduces the thickness of steel in the practical application, is used for the steel of packing in the industries such as food, chemical industry, needs to reduce thickness.But the minimizing of steel thickness can not be to affect user's use properties, therefore, industry to the requirement of steel is at present: in the material attenuate, the intensity of material also should improve, also just say in order to guarantee the supporting capacity of product, when reducing material thickness, must improve strength of materials value.
The secondary cold-rolling product has the characteristics of intensity height, thinner thickness, guaranteeing that for the final user under the end product quality prerequisite, attenuate uses the thickness of material, the reduction tank plays decisive role with the consumption of material, thereby secondary cold-rolling is widely used in association area.
The secondary cold rolled material production technique is to use the effect of rolling of secondary cold-rolling to increase and realize target intensity mostly at present, thereby satisfies the purpose of attenuate enhancing degree, and such production technique meeting is so that the secondary cold-rolling deformation rate is very large, and rolling specs also can be restricted.Along with the gradually raising of reduced thickness material to the rolling requirement of secondary cold-rolling, wish to obtain a kind of material of attenuate enhancing degree, it can reduce rolling load when secondary cold-rolling is rolling, and makes steel can satisfy the production requirement of tank product strength processed under the baking hardening effect after the zinc-plated chromium plating application of secondary cold-rolling.
Summary of the invention
One of purpose of the present invention is to provide a kind of secondary cold-rolling steel, and it can obtain good baking and hardening performance and processing characteristics, and can satisfy the requirement of high strength attenuate material.
Another object of the present invention is to provide a kind of manufacture method of secondary cold-rolling steel, this manufacture method can improve the baking and hardening performance of steel after application by rational technological design, it has solved the property the manufactured problem of high-strength attenuate steel, and production cost is lower and the quality of production stable.
One of for achieving the above object, the invention provides a kind of secondary cold-rolling steel, its chemical element quality percentage composition is:
C：0.005～0.015%，
Mn：0.50～1.00%，
Al：0.01～0.04%，
N：0.004～0.01%，
Surplus is Fe and other inevitable impurity.
In order to make secondary cold-rolling steel of the present invention can produce after the application preferably baking hardening effect, corresponding chemical element Composition Design principle is as follows:
C: because C exists with the form of interstitial atom and cementite, in steel, have strengthening effect in steel.In order to strengthen steel, the carbon that need to keep certain content improves the intensity of steel, simultaneously, consider pinning effect that carbon exists with interstitial atom so that steel is more obvious when possessing baking hardening effect, particularly carbon content in 0.010% left and right sides when application.If carbon content is too low, then do not have and strengthen and the baking hardening effect, carbon content is too high, though can obtain higher baking hardening value, the welding property of steel can variation.Therefore, C content of the present invention should be controlled in the scope between 0.005～0.015%.
Mn: identical with the C element, Mn also is the strengthening element of steel, in steel, suitably add the raising that a small amount of Mn is conducive to steel intensity, the Mn that adds simultaneously can with impurity element S in conjunction with generating MnS, hot-short to reduce the surface, avoid the generation of surface quality problems, so the content of Mn element should be controlled to be 0.50～1.00% among the present invention.
Al:Al adds when making steel step as reductor, and it can be conducive to material surface quality and processing characteristics.When Al less than 0.01% the time, free oxygen level in the molten steel is higher, can affect the purity of molten steel, cause the surface quality of steel and cause its poor processability, and when Al greater than 0.04% the time, too much Al addition is separated out excessively the N of steel, and the minimizing of interstitial atom N is unfavorable to the baking and hardening performance of steel.So, the quality percentage composition of Al element among the present invention is designed to 0.01～0.04%.
N: because N exists with the form of interstitial atom and AlN, in steel, have very strong strengthening effect in steel, should consider also that simultaneously pinning effect that N exists with interstitial atom is so that steel possesses the effect of baking hardening.When N was very few, the baking hardening effect of steel was not enough, and when N was too much, the baking hardening effect of steel was too high, the processing characteristics behind the deteriorated coating steel plate of meeting.So the N among the present invention need to be controlled between 0.004 to 0.01% scope.
Impurity element in the technical program mainly is P element and S element, and its content is lower, and the processibility of steel is better.Although P can improve the intensity of steel, P also can cause fragility and deteriorated its solidity to corrosion of steel; S is harmful element to steel, can produce a large amount of inclusiones, affects the toughness of steel; Particularly unfavorable in the flange of later process and so on secondary workability, solidity to corrosion to tank processed field, so that the content of P and S needs is low as much as possible.
In order to realize another purpose of foregoing invention, the present invention also correspondingly provides a kind of manufacture method of secondary cold-rolling steel, and it comprises step successively: smelting, refining, hot rolling reeling, pickling, cold rolling, continuous annealing and secondary cold-rolling step.
The manufacture method of secondary cold-rolling steel of the present invention cooperates above-mentioned Composition Design, and the secondary cold-rolling steel that produces has needed baking and hardening performance and processing characteristics.
Further, in the manufacture method of above-mentioned secondary cold-rolling steel, also has the finishing step after the described secondary cold-rolling step.
Further, in the manufacture method of above-mentioned secondary cold-rolling steel, in the hot rolling reeling step, with extremely 〉=1180 ℃ of heating of plate blanks.
In the hot rolling reeling step, control Heating temperature 〉=1180 ℃ are because the hot rolling Heating temperature is higher, C in the material, the solid solution of N atom are more, the hardness of steel is also just higher, and AlN begins solvent temperature about 1150 ℃, so, with Heating temperature 〉=1180 ℃, guarantee that AlN can access more sufficient solid solution.
Further, in the manufacture method of above-mentioned secondary cold-rolling steel, in the hot rolling reeling step, control finishing temperature 〉=Ar
3Temperature.
The reason that finishing temperature has adopted the temperature that is higher than Ar3 to be rolled is: when finishing temperature is too high, can produce easily iron scale, cross when low when finishing temperature, be difficult for making carbon dissolution in austenite, thereby finishing temperature is controlled at 〉=the Ar3 temperature.
Further, in the manufacture method of above-mentioned secondary cold-rolling steel, in the hot rolling reeling step, control coiling temperature≤600 ℃.
If coiling temperature is during greater than 600 ℃, AlN then can excessively separate out, and causes that finished product hardness is low, the baking hardening value is low, so coiling temperature is controlled at≤600 ℃.
Further, in the manufacture method of above-mentioned secondary cold-rolling steel, in the continuous annealing step, 600～700 ℃ of control annealing temperatures.
In the continuous annealing step, because annealing temperature is quite large on the impact of steel finished product hardness, its baking hardening value is also produced certain impact, when annealing temperature is too low, the steel much higher hard, poor processability, but when annealing temperature is too high, steel hardness is on the low side again, and correspondingly its baking hardening value is also on the low side; So annealing temperature is controlled between 600 ~ 700 ℃ the scope.
Further, in the manufacture method of above-mentioned secondary cold-rolling steel, in the secondary cold-rolling step, control secondary cold-rolling rate is 5～25%.
The secondary cold-rolling deformation rate all has significant impact to hardness and the baking hardening value of steel, increase along with the secondary cold-rolling deflection, the hardness of steel increases and its baking hardening value decline, excessive secondary cold-rolling rate can make the baking hardening value of steel descend, too little secondary cold-rolling rate can make steel can not get needed hardness, and produce easily timeliness generation slip line, so the secondary cold-rolling rate in the manufacture method of the present invention is controlled at 5～25%.
Because secondary cold rolled material is mainly used in the higher seamless tin of hardness, Three piece Can body and tank deck bottom purposes, it has certain anti-external and internal pressure requirement, therefore, not only require the hardness of steel high but also need steel to possess certain punch process and weldability are arranged.But, improve the method that starting material hardness adopts in the prior art or be when Composition Design, to add the element such as too much carbon, be the secondary cold-rolling rate that in technical process, strengthens, and these two kinds of methods all can have a negative impact for the manufacturing of steel and processing characteristics and the welding property of use.And secondary cold-rolling steel of the present invention is in reasonable component design and adopt in the situation of less secondary cold-rolling deflection, and the hardness that compares to secondary cold-rolling of the prior art through the hardness after the zinc-plated chromium plating application increases.
Compared with prior art, secondary cold-rolling steel of the present invention, alloying constituent content is few, have higher intensity and hardness and good processing characteristics, this secondary cold-rolling steel possesses the baking and hardening performance of high-quality after the process application, the requirement of the high-strength attenuate that association area proposes the steel that is applied to tank processed packing can be satisfied, the fields such as food, chemical industry, household chemicals and electronic product can be widely used in.
The manufacture method of secondary cold-rolling steel of the present invention; compare to prior art; the reasonable component design is matched with the manufacturing step of improvement, by the interstitial atom strengthening effect, in the situation that adopts less secondary cold-rolling deflection; just can obtain the intensity height; thin thickness, baking and hardening performance and processing characteristics be excellent steel all, and production cost is lower; plate quality is stable, and the factory and the enterprise that are suitable for each field carry out the production operation of industrialization, large-scale.
Embodiment
Below in conjunction with specific embodiment technical solutions according to the invention are described in further detail.
Embodiment A-D and Comparative Example E-F
Make secondary cold-rolling steel of the present invention according to following step:
(1) converter smelting, the proportioning of controlling each chemical element is as shown in table 1;
(2) furnace rear refining;
(3) hot rolling: with extremely 〉=1180 ℃ of heating of plate blanks, finishing temperature 〉=Ar
3Temperature, coiling temperature≤600 ℃;
(4) pickling;
(5) cold rolling: cold rolling draft is 50～90%;
(6) continuous annealing: 600～700 ℃ of annealing temperatures;
(7) secondary cold-rolling: the secondary cold-rolling rate is 5～25%.
(8) finishing finished product volume.
The quality per distribution ratio (wt.%) of each component of the secondary cold-rolling steel among table 1 embodiment A-D and the Comparative Example E-F
| Title | C | Mn | P | S | Al | N |
| Embodiment A | 0.010 | 0.8 | 0.011 | 0.005 | 0.028 | 0.0055 |
| Embodiment B | 0.015 | 1.0 | 0.008 | 0.010 | 0.035 | 0.0086 |
| Embodiment C | 0.006 | 0.9 | 0.013 | 0.007 | 0.031 | 0.0063 |
| Embodiment D | 0.009 | 0.5 | 0.012 | 0.008 | 0.025 | 0.0098 |
| Comparative Example E | 0.10 | 0.4 | 0.011 | 0.006 | 0.063 | 0.0038 |
| Comparative Example F | 0.08 | 0.3 | 0.013 | 0.010 | 0.058 | 0.0041 |
Table 2 has shown that the concrete technology parameter of each embodiment and each comparative example reaches.Wherein, the routine concrete technology parameter of each in the table 2 is corresponding to corresponding embodiment and comparative example in the table 1.
Concrete technology parameter in the manufacturing process of table 2 embodiment A-D and Comparative Example E-F
| Title | Heating temperature (℃) | Finishing temperature (℃) | Coiling temperature (℃) | Annealing temperature (℃) | Secondary cold-rolling rate (%) |
| The present invention | ≥1180 | ≥Ar 3Temperature | ≤600 | 600~700 | 5～25 |
| Embodiment A | 1230 | 871 | 550 | 620 | 8 |
| Embodiment B | 1180 | 865 | 530 | 695 | 25 |
| Embodiment C | 1220 | 889 | 570 | 650 | 15 |
| Embodiment D | 1250 | 890 | 580 | 600 | 10 |
| Comparative Example E | 1150 | 865 | 580 | 630 | 30 |
| Comparative Example F | 1170 | 870 | 560 | 650 | 26 |
Table 3 has shown the mechanical property of the secondary cold-rolling steel that embodiment A-D in the technical program and Comparative Example E-F are related.
The relevant mechanical property parameters of table 3 secondary cold-rolling steel
| Title | Hardness (HR30T) before the baking | Hardness (HR30T) after the baking | BH value (MPa) |
| The present invention | 60~80 | 60~80 | ≥20 |
| Embodiment A | 62 | 65 | 36 |
| Embodiment B | 73 | 75 | 25 |
| Embodiment C | 68 | 70 | 31 |
| Embodiment D | 65 | 68 | 42 |
| Comparative Example E | 74 | 74 | 3 |
| Comparative Example F | 71 | 72 | 6 |
* annotate: BH is Bake Hard, the baking hardening value.Hardness in the table 3 and BH value adopt general GB standard testing, baking condition: 170 ℃ * 20min.
Associative list 2, as can be seen from Table 3, the secondary cold-rolling rate that embodiment A-D adopts is between the 5-25% scope, and the secondary cold-rolling rate of embodiment E-F is more than 25%, be different from the larger secondary cold-rolling deformation quantity of comparative example, the equal less of the Cold Reduction of embodiment, thereby the rolling load amount in the time of can reducing secondary cold-rolling; The hardness of the related hardness of secondary cold-rolling steel after baking of embodiment A-D before the baking all has corresponding raising, and the related hardness of secondary cold-rolling steel before and after baking of Comparative Example E-F does not produce very large variation, and these explanation technical solutions according to the invention are conducive to the lifting of secondary cold-rolling steel hardness; The BH value of the secondary cold-rolling steel that embodiment A-D is related surpasses 20Mpa, and it is much higher than the BH value of Comparative Example E-F, and this has illustrated that secondary cold-rolling steel of the present invention has good baking and hardening performance.
Those of ordinary skill in the art will be appreciated that, above embodiment illustrates the present invention, and be not to be used as limitation of the invention, as long as in connotation scope of the present invention, all will drop in claims scope of the present invention variation, the modification of the above embodiment.
Claims (8)
1. a secondary cold-rolling steel is characterized in that, its chemical element quality percentage composition is:
C：0.005～0.015%，
Mn:0.50～1.00%，
Al:0.01～0.04%，
N:0.004～0.0100%，
Surplus is Fe and other inevitable impurity.
2. the manufacture method of secondary cold-rolling steel as claimed in claim 1 is characterized in that, comprises successively step: smelting, refining, hot rolling reeling, pickling, cold rolling, continuous annealing and secondary cold-rolling step.
3. the manufacture method of secondary cold-rolling steel as claimed in claim 2 is characterized in that, also has the finishing step after the described secondary cold-rolling step.
4. the manufacture method of secondary cold-rolling steel as claimed in claim 2 or claim 3 is characterized in that, in the hot rolling reeling step, with heating of plate blank to 〉=1180 ℃.
5. the manufacture method of secondary cold-rolling steel as claimed in claim 2 or claim 3 is characterized in that, in the hot rolling reeling step, and control finishing temperature 〉=Ar
3Temperature.
6. the manufacture method of secondary cold-rolling steel as claimed in claim 2 or claim 3 is characterized in that, in the hot rolling reeling step, and control coiling temperature≤600 ℃.
7. the manufacture method of secondary cold-rolling steel as claimed in claim 2 or claim 3 is characterized in that, in the continuous annealing step, and 600～700 ℃ of control annealing temperatures.
8. the manufacture method of secondary cold-rolling steel as claimed in claim 2 or claim 3 is characterized in that, in the secondary cold-rolling step, control secondary cold-rolling rate is 5～25%.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111748729A (en) * | 2019-03-27 | 2020-10-09 | 宝山钢铁股份有限公司 | Steel sheet for lid manufacture having excellent sealing properties and internal pressure resistance, and method for producing same |
| CN115125434A (en) * | 2021-03-29 | 2022-09-30 | 宝山钢铁股份有限公司 | Low-carbon high-nitrogen tinned substrate and continuous slab casting production method thereof |
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| CN115125434A (en) * | 2021-03-29 | 2022-09-30 | 宝山钢铁股份有限公司 | Low-carbon high-nitrogen tinned substrate and continuous slab casting production method thereof |
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Application publication date: 20130417 |